Temperature and field stable relaxor-PT piezoelectric single crystals

ABSTRACT

The application is directed to piezoelectric single crystals having shear piezoelectric coefficients with enhanced temperature and/or electric field stability. These piezoelectric single crystal may be used, among other things, for vibration sensors as well as low frequency, compact sonar transducers with improved and/or enhanced performance.

CROSS-REFERENCE TO RELATED APPLICATION

This application claims the benefit of, and is a divisional application of co-pending U.S. patent application Ser. No. 13/206,971, now allowed, entitled “TEMPERATURE AND FIELD STABLE RELAXOR-PT PIEZOELECTRIC SINGLE CRYSTALS”, and filed Aug. 10, 2011, which claims priority to and the benefit of U.S. Provisional Application No. 61/372,439, filed Aug. 10, 2010, both of which are hereby incorporated by reference in their entirety.

STATEMENT OF FEDERALLY SPONSORED RESEARCH

Portions of the invention disclosed herein were reduced to practice with the support of the U.S. Office of Naval Research, Contract No. N00014-07-C-0858. The U.S. Government may have certain rights in this invention.

FIELD

The present invention is generally directed to ferroelectric materials, and more particularly to relaxor-PT based piezoelectric single crystals.

BACKGROUND

For the past 50 years, perovskite Pb(Zr_(x)Ti_(1-x))O₃ (PZT) piezoelectric ceramics have dominated the commercial market of electronic devices, including piezoelectric sensors, actuators and medical ultrasonic transducers, due to their high piezoelectric and electromechanical coupling factors. For example, the shear piezoelectric coefficient d₁₅ and electromechanical coupling factor k₁₅ for PZT5A type (DOD Type II) materials are found to be on the order of about 400 pC/N and approximately 70%, respectively. Innovations in electronic devices have been the driving force for new developments in piezoelectric materials, including relaxor-PT single crystals.

The excellent piezoelectric properties of relaxor-PT single crystals, including Pb(Mg_(1/3)Nb_(2/3))O₃—PbTiO₃ (“PMN-PT”) and Pb(In_(0.5)Nb_(0.5))O₃—Pb(Mg_(1/3)Nb_(2/3))O₃—PbTiO₃ (“PIN-PMN-PT”), have attracted considerable interest over the last decade, particularly for applications in high performance medical transducers. However, their commercial use has been limited due to high variation of the dielectric and piezoelectric properties with temperature. Furthermore, the low coercive field of current relaxor-PT crystals further limits their application.

Single crystal compositions near their respective morphotropic phase boundaries (MPB) exhibit longitudinal piezoelectric coefficients (d₃₃) greater than 1500 pC/N with electromechanical coupling factors higher than 90% along the pseudo-cubic <001> directions. These excellent properties make relaxor-PT single crystals promising candidates for broadband and high sensitivity ultrasonic transducers, sensors and other electromechanical devices. Specifically, certain applications of sensors and transducers, such as accelerometers, vector sensors and non-destructive evaluation (NDE) transducers, require large shear coefficients d₁₅.

It has been reported that rhombohedral single domain PMN-PT crystals poled along their spontaneous polarization direction [111], which may be referred to as having the engineered domain configuration ‘1R’, where ‘1’ represents a single domain crystal and ‘R’ represents the rhombohedral phase, possess high shear values. For these materials, piezoelectric coefficients, d₁₅, and shear coupling factors, k₁₅, are reported to be >2000 pC/N and >90%, respectively, due to the polarization rotation facilitated by the single domain state. Unfortunately, shear piezoelectric coefficients are found to increase significantly with increasing temperature, with more than a 200% change from room temperature to their respective ferroelectric phase transition temperatures. Hence, this strong temperature dependence severely limits their implementation in many electromechanical devices. Furthermore, relaxor-PT single crystals exhibit coercive fields on the order of <2-5 kV/cm, thus limiting applications requiring large AC fields, such as NDE transducers and high power sonar.

What is needed is a piezoelectric single crystal that does not suffer from one or more of the above drawbacks.

SUMMARY

According to certain exemplary embodiments, problems with known relaxor-PT single crystals are overcome by providing crystals having a large shear piezoelectric coefficient d₂₄ achieved through monoclinic/orthorhombic relaxor-PT single crystals with ‘1O’ single domain configuration. Such crystals have been found to possess nearly temperature independent behavior over the temperature range of −50° C. to the orthorhombic to tetragonal phase transition temperature, generally on the order of about 75° C. to about 105° C.

Tetragonal and/or doped relaxor-PT crystals were found to possess high coercive fields and/or internal bias fields while keeping very high shear piezoelectric coefficients comparable to the values of single domain rhombohedral relaxor-PT crystals, providing crystals that can be driven in shear under a high AC field.

Single crystals with ‘2R’ or ‘1O’ domain configuration and/or doped relaxor-PT crystals were also found to possess zero thickness shear piezoelectric coefficients d₁₆ while keeping very high shear piezoelectric coefficients d₁₅ comparable to the values of ‘1R’ single domain rhombohedral relaxor-PT crystals.

Rotation of face (contour) shear d₃₆ single crystals with ‘2R’ domain configuration and/or relaxor-PT crystals around the crystallographic axes were found to eliminate or minimize one of the transverse width extensional piezoelectric coefficients.

The high shear piezoelectric properties of relaxor-PT single crystals with new engineered domain configurations in accordance with exemplary embodiments disclosed herein are promising for various electromechanical device applications, such as vector sensors, non-destructive evaluation (NDE) transducers and low frequency sonar transducers, to name a few.

According to an exemplary embodiment, a piezoelectric single crystal has a composition of the formula (1-x)Pb(Mg_(1/3)Nb_(2/3))O₃-xPbTiO₃ (“PMN-xPT”) or yPb(In_(1/2)Nb_(1/2))O₃-(1−y−z) Pb(Mg_(1/3)Nb_(2/3))O₃-zPbTiO₃ (“yPIN-(1−y−z)PMN-zPT”), where 0.305≦x≦0.355, 0.26<y≦0.50, 0.31<z≦0.36. The crystal is poled along the crystallographic [110] direction and has an orthorhombic/monoclinic phase and ‘1O’ single domain state.

According to another exemplary embodiment, a piezoelectric single crystal has the formula PMN-xPT or yPIN-(1−y−z)PMN-zPT, where 0.20<x≦0.305, 0.26<y≦0.50, 0.20<z≦0.31. The crystal is poled along the crystallographic [110] direction and has a rhombohedral phase, a ‘2R’ engineered domain configuration and macroscopic mm2 symmetry.

According to another exemplary embodiment, a piezoelectric single crystal has the formula PMN-xPT or yPIN-(1−y−z)PMN-zPT, where x>0.355, 0.26<y≦0.50, z>0.36. The crystal is poled along the crystallographic [001] direction and has a ‘1T’ single domain state and macroscopic 4 mm symmetry.

According to another exemplary embodiment, a ternary piezoelectric single crystal PIN-PMN-PT with rhombohedral phase is provided wherein the crystal is poled along the crystallographic [111] direction and rotated to provide a shear piezoelectric coefficient d₁₆ that is less than about 100 pC/N.

An advantage of exemplary embodiments is that a piezoelectric single crystal is provided having shear piezoelectric coefficients with temperature stability.

Another advantage of exemplary embodiments is that a piezoelectric single crystal is provided with improved AC field drive stability.

Still another advantage of exemplary embodiments is that piezoelectric single crystals are provided having shear piezoelectric coefficients that are more stable in temperature and/or electric field than previously known single crystals. Such single crystals in accordance with exemplary embodiments may be used, for example, as vibration sensors as well as low frequency, compact sonar transducers with improved and/or enhanced performance.

Other features and advantages will be apparent from the following more detailed description of exemplary embodiments, taken in conjunction with the accompanying drawings which illustrate, by way of example, the principles of the invention.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 is a schematic phase diagram for relaxor-PT based crystals, where R, O and T represent rhombohedral, orthorhombic/monoclinic and tetragonal phase regions.

FIG. 2 is a schematic of various shear mode samples.

FIG. 3 shows two independent shear piezoelectric modes (15- and 24-) and related polarization rotation paths in orthorhombic crystals.

FIG. 4 shows the temperature dependence of shear piezoelectric coefficients for orthorhombic relaxor-PT based single crystals.

FIG. 5(a) shows the polarization hysteresis for pure d₁₅ [110]/(−110) PIN-PMN-PT crystals with ‘2R’ engineered domain configuration.

FIG. 5(b) shows the polarization loops for the first and 5000th cycles at different electric field drive levels for pure d₁₅ [110]/(−110) PIN-PMN-PT crystals with ‘2R’ engineered domain configuration.

FIG. 5(c) shows the impedance characteristics for shear thickness vibration mode after cycles at different levels for pure d₁₅ [110]/(−110) PIN-PMN-PT crystals with ‘2R’ engineered domain configuration.

FIG. 6(a) shows the polarization hysteresis for manganese doped d₁₅ [110]/(−110) PIN-PMN-PT crystals with ‘2R’ engineered domain configuration.

FIG. 6(b) shows the polarization loops for the first and 5000th cycles at different electric field drive levels for manganese doped d₁₅ [110]/(−110) PIN-PMN-PT crystals with ‘2R’ engineered domain configuration.

FIG. 6(c) shows the impedance characteristics for shear thickness vibration mode after cycles at different levels for manganese doped d₁₅ [110]/(−110) PIN-PMN-PT crystals with ‘2R’ engineered domain configuration.

FIG. 7(a) shows the polarization hysteresis for pure d₁₅ [110]/(−110) PIN-PMN-PT crystals with ‘1O’ engineered domain configuration.

FIG. 7(b) shows polarization loops for the first and 5000th cycles at different electric field drive levels for pure d₁₅ [110]/(−110) PIN-PMN-PT crystals with ‘1O’ engineered domain configuration.

FIG. 7(c) shows impedance characteristics for shear thickness vibration mode after cycles at different levels for pure d₁₅ [110]/(−110) PIN-PMN-PT crystals with ‘1O’ engineered domain configuration.

FIG. 8(a) shows polarization hysteresis for manganese doped d₁₅ [110]/(−110) PIN-PMN-PT crystals with ‘1O’ engineered domain configuration.

FIG. 8(b) shows polarization loops for the first and 5000th cycles at different electric field drive levels for manganese doped d₁₅ [110]/(−110) PIN-PMN-PT crystals with ‘1O’ engineered domain configuration.

FIG. 8(c) shows impedance characteristics for shear thickness vibration mode after cycles at different levels for manganese doped d₁₅ [110]/(−110) PIN-PMN-PT crystals with ‘1O’ engineered domain configuration.

FIG. 9(a) shows polarization hysteresis for pure [001]/(100) PIN-PMN-PT crystals with ‘1T’ engineered domain configuration.

FIG. 9(b) shows polarization loops for the first and 5000th cycles at different electric field drive levels for pure [001]/(100) PIN-PMN-PT crystals with ‘1T’ engineered domain configuration.

FIG. 9(c) shows impedance characteristics for shear thickness vibration mode after cycles at different levels for pure [001]/(100) PIN-PMN-PT crystals with ‘1T’ engineered domain configuration.

FIG. 10(a) shows polarization hysteresis for manganese doped [001]/(100) PIN-PMN-PT crystals with ‘1T’ engineered domain configuration.

FIG. 10(b) shows polarization loops for the first and 5000th cycles at different electric field drive levels for manganese doped [001]/(100) PIN-PMN-PT crystals with ‘1T’ engineered domain configuration.

FIG. 10(c) shows impedance characteristics for shear thickness vibration mode after cycles at different levels for manganese doped [001]/(100) PIN-PMN-PT crystals with ‘1T’ engineered domain configuration.

FIG. 11(a) shows polarization hysteresis for manganese doped [001]/(110) PIN-PMN-PT crystals with ‘1T’ engineered domain configuration.

FIG. 11(b) shows polarization loops for the first and 5000th cycles at different electric field drive levels for manganese doped [001]/(110) PIN-PMN-PT crystals with ‘1T’ engineered domain configuration.

FIG. 11(c) shows impedance characteristics for shear thickness vibration mode after cycles at different levels for manganese doped d₁₅ [001]/(110) PIN-PMN-PT crystals with ‘1T’ engineered domain configuration.

FIG. 12(a) shows the polarization hysteresis for pure d₁₅ [111]/(1-10) PIN-PMN-PT crystals with ‘1R’ engineered domain configuration.

FIG. 12(b) shows the polarization loops for the first and 5000th cycles at different electric field drive levels for pure d₁₅ [111]/(1-10) PIN-PMN-PT crystals with ‘1R’ engineered domain configuration.

FIG. 12(c) shows the impedance characteristics for shear thickness vibration mode after cycles at different levels for pure d₁₅ [111]/(1-10) PIN-PMN-PT crystals with ‘1R’ engineered domain configuration.

FIG. 13(a) shows the polarization hysteresis for manganese doped d₁₅ [111]/(1-10) PIN-PMN-PT crystals with ‘1R’ engineered domain configuration.

FIG. 13(b) shows the polarization loops for the first and 5000th cycles at different electric field drive levels for manganese doped d₁₅ [111]/(1-10) PIN-PMN-PT crystals with ‘1R’ engineered domain configuration.

FIG. 13(c) shows the impedance characteristics for shear thickness vibration mode after cycles at different levels for manganese doped d₁₅ [111]/(1-10) PIN-PMN-PT crystals with ‘1R’ engineered domain configuration.

FIG. 14 shows rotation about the X axis to reduce or eliminate the d₁₆ coefficient while maintaining polarization in the <111> axis for d₁₅ [111]/(1-10) PIN-PMN-PT crystals with ‘1R’ engineered domain configuration.

FIG. 15 the measured d₁₅ and d₁₆ shear piezoelectric coefficients for d₁₅ [111]/(1-10) PIN-PMN-PT crystals with ‘1R’ domain configuration rotated about the X axis at angles from −26° to +26°.

FIG. 16 shows the measured d₁₅ and d₁₆ shear strain field curves for [110]/(−110) PMN-PT crystal with ‘2R’ engineered domain configuration

FIG. 17 shows the measured d₁₅ and d₁₆ shear strain field curves for d₁₅ [110]/(−110) PIN-PMN-PT crystal with ‘2R’ engineered domain configuration.

FIG. 18 shows the measured d₁₅ and d₁₆ shear strain field curves for d₁₅ manganese modified [110]/(−110) PIN-PMN-PT crystal stack of three bonded plates with ‘2R’ engineered domain configuration.

FIG. 19 shows a d₃₆ face shear [110]/(110) single crystal with ‘2R’ engineered domain configuration and a rotated angle theta that eliminates one of the transverse width extensional piezoelectric coefficients d₃₁′ or d₃₂′.

FIG. 20 shows the measured d₃₁′ and d₃₂′ strain field curves for a d₃₆ face shear [110]/(110) PMN-PT single crystal with ‘2R’ engineered domain configuration, showing near elimination of the d₃₂′.

It will be appreciated that in figures showing more than one line on a graph, identifiers are used to aid in differentiation, although the specific location of an identifier along the line is not necessarily intended to correspond to any particular data point.

DETAILED DESCRIPTION OF EXEMPLARY EMBODIMENTS

Exemplary embodiments provide for composition ranges and crystallographic orientations of piezoelectric single crystals where the shear piezoelectric coefficients are more stable in temperature and/or electric field. The disclosed piezoelectric single crystals may be used, for example, as vibration sensors and low frequency, compact sonar transducers with improved and/or enhanced performance.

It has been discovered that composition ranges and crystal cuts in accordance with exemplary embodiments give rise to certain crystal structures with increased shear coefficients. It has further been discovered that these crystal structures, composition ranges, and crystal cuts result in an unexpected improvement in shear property stability.

It has also been discovered that composition ranges and crystal cuts in accordance with exemplary embodiments give rise to certain crystal structures with eliminated or minimized transverse shear coefficients or width extensional coefficients.

Accordingly, exemplary embodiments are directed to composition ranges, crystal structures, and properties described herein that have high shear temperature stability and/or AC field stability. As used herein, the letters R, O and T refer to a domain state having a rhombohedral, orthorhombic/monoclinic, or tetragonal phase, respectively, while a leading number in front of that letter refers to the number of domains present, which may be a single domain (i.e., a leading 1) or multi-domain (e.g., a leading 2, 3 or 4).

Generally, embodiments relate to a piezoelectric single crystal having a composition with the formula (1-x)Pb(Mg_(1/3)Nb_(2/3))O₃-xPbTiO₃ (“PMN-xPT”) or yPb(In_(1/2)Nb_(1/2))O₃-(1−y−z) Pb(Mg_(1/3)Nb_(2/3))O₃-zPbTiO₃ (“yPIN-(1−y−z)PMN-zPT”), where x>0.2, 0.26≦y≦0.50, and z>0.2, the crystal having a multi-domain rhombohedral, single-domain orthorhombic/monoclinic or tetragonal phase and a finite piezoelectric shear coefficient or to a piezoelectric single crystal having a composition with the formula yPIN-(1−y−z)PMN-zPT, where 0.26≦y≦0.50, z>0.2, the crystal having a single-domain rhombohedral phase and a finite piezoelectric shear coefficient.

In one embodiment, a piezoelectric single crystal has a composition of the formula PMN-xPT or yPIN-(1−y−z)PMN-zPT, where 0.305<x≦0.355, 0.26≦y≦0.50, 0.31<z≦0.36. The crystal has an orthorhombic/monoclinic phase. The crystal is poled along the crystallographic [110] direction and has a ‘1O’ single domain state. The crystal exhibits temperature-stable piezoelectric shear properties.

In a further embodiment, x=0.32, y=0.26, z=0.33 and the crystal has macroscopic mm2 symmetry. In some embodiments, with electrodes on the (001) faces of the crystal, the crystal has a shear vibration with a k₂₄ of about 85% and a shear piezoelectric coefficient d₂₄ of about 2000pC/N. The shear piezoelectric coefficient d₂₄ is substantially stable in temperature range of −50° C. to about T_(OT), where the T_(OT) is orthorhombic to tetragonal phase transition temperature.

In another embodiment having this composition but in which electrodes are on the (−110) faces, the crystal has a k₁₅ of about 90% and a shear piezoelectric coefficient d₁₅ of about 3000 pC/N. In such cases, the shear mode properties of yPIN-(1−y−z)PMN-zPT shows particular improved AC field stability under high drive. The coercive field is about 5 kV/cm for pure (i.e., undoped) crystals, the allowable AC field drive level of pure crystal is 40% of coercive fields, being on the order of about 2kV/cm.

In another embodiment, the piezoelectric single crystal previously described is doped with between about 0.2 mol % and about 8 mol % of a dopant selected from the group consisting of manganese, iron, cobalt, nickel, aluminum, gallium, copper, potassium sodium, fluorides and combinations thereof. In one embodiment, the dopants are provided by introducing one or more of the following compounds into the composition: MnO₂, MnCO₃, Fe₂O₃, Co₂O₃, CoCO₃, Ni₂O₃, NiCO₃, Al₂O₃, Ga₂O₃, Cu₂O, CuO, K₂CO₃, Na₂CO₃, fluoride and/or combinations thereof. Single crystals having such doped compositions also result in temperature stable piezoelectric shear properties. Preferably, the dopant is present at about 1 mol % to about 3 mol % and in some preferred embodiments, the dopant is manganese (introduced, e.g., by MnO₂ and/or MnCO₃). In one embodiment, x=0.32, y=0.26, z=0.33 and the crystal is doped with about 1.5 mol % manganese.

As with the pure orthorhombic/monoclinic crystal, the doped crystal may be poled along the [110] crystallographic direction to achieve a ‘1O’ single domain state with macroscopic mm2 symmetry. In an embodiment having this composition, the crystal has electrodes on the (001) faces, a k₂₄ of about 85% and a shear piezoelectric coefficient d₂₄ of about 2000 pC/N. The shear piezoelectric coefficient d₂₄ was substantially stable in the usage temperature range of −50° C. to about T_(OT).

In another embodiment this composition, the crystal may be poled along the [110] crystallographic direction and has electrodes on the (−110) faces, and has a k₁₅ of about 90% and a shear piezoelectric coefficient d₁₅ of about 3000 pC/N. The shear mode properties of yPIN-(1-y-z)PMN-zPT in particular showed improved AC field stability under high drive. The coercive field is further increased to about 7 to 9 kV/cm for such doped crystals, with internal bias field of about 1 kV/cm. The allowable AC field drive level of the doped crystals is 60-70% of their respective coercive fields, being on the order of about 4 to 6 kV/cm, due to the internal bias.

In one embodiment, a piezoelectric single crystal has a composition of the formula PMN-xPT or yPIN-(1−y−z)PMN-zPT, where x≧0.355, 0.26≦y≦0.50, z≧0.36, the crystal poled along the [001] direction. The crystal has a tetragonal phase, having a ‘1T’ single domain state and macroscopic 4 mm symmetry. In one embodiment, x=0.36, y=0.26, and z=0.37.

In one embodiment of the tetragonal crystal, electrodes are on the (100) and/or (110) faces, with a k₁₅ of about 75-85% and a d₁₅ of about 1000-2500 pC/N. In such embodiments, the shear mode properties of yPIN-(1−y−z)PMN-zPT crystals in particular has improved AC field stability under high drive. The coercive field is >11 kV/cm, with an allowable AC field drive level that is about 40% of coercive fields, being on the order of about 4-5kV/cm.

In another embodiment, the piezoelectric single crystal previously described is doped with between about 0.2 mol % and about 8 mol % of a dopant selected from the group consisting of manganese, iron, cobalt, nickel, aluminum, gallium, copper, potassium sodium, fluorides and combinations therefore. The dopants may be provided by introducing one or more of the following compounds into the composition: MnO₂, MnCO₃, Fe₂O₃, Co₂O₃, CoCO₃, Ni₂O₃, NiCO₃, Al₂O₃, Ga₂O₃, Cu₂O, CuO, K₂CO₃, Na₂CO₃, fluoride and/or combinations thereof. Such single crystals having such doped compositions also result in temperature-stable piezoelectric shear properties. Preferably, the dopant is present at between about 1 mol % and about 3 mol % and in some preferred embodiments, the dopant is manganese (introduced, e.g., by MnO₂ and/or MnCO₃). In one embodiment, x=0.36, y=0.26, and z=0.37 and the crystal is doped with 1.5 mol % manganese.

In an embodiment where the doped tetragonal crystal has electrodes on the (100) and/or (110) faces, k₁₅ of about 75-85% and d₁₅ of about 1000-2500 pC/N, the shear mode properties of yPIN-(1−y−z)PMN-zPT crystals in particular has improved AC field stability under high drive. The coercive field is >11 kV/cm for doped crystals, with internal bias field of about 1-2 kV/cm. The allowable AC field drive level is between about 60 and about 70% of their respective coercive fields, being on the order of about 7-8kV/cm, due to the internal bias.

In yet another embodiment, a piezoelectric single crystal has a composition of the formula PMN-xPT or yPIN-(1−y−z)PMN-zPT, where 0.20≦x≦0.305, 0.26≦y≦0.50, 0.20≦z≦0.31. The crystal is in the rhombohedral phase. The crystal is poled along the crystallographic <110> direction, has a ‘2R’ engineered domain configuration and macroscopic mm2 symmetry.

In another embodiment having of this composition, the crystal is poled along the crystallographic direction and electrodes on the (−110) faces. The crystal has no or minimal transverse piezoelectric coefficient d₁₆ (i.e., the absolute value of d₁₆ is less than about 100 pC/N, preferably less than about 50 pC/N).

In another embodiment having this composition, the crystal is poled along the [110] crystallographic direction, has electrodes on the (110) faces, and the crystal is rotated around the Z-axis (i.e., the poling axis, as will be appreciated by those of ordinary skill). The crystal has a face shear component piezoelectric coefficient d₃₆ that is dependent on the transverse width extensional piezoelectric coefficients d₃₁ and d₃₂ of the crystal before rotation. The crystal further exhibits an elimination or reduction of the rotated transverse width extensional piezoelectric coefficients d₃₁′ or d₃₂′ (i.e., the absolute value of the minimized rotated transverse width extensional piezoelectric coefficient is less than or equal to about 50 pC/N, preferably less than about 25 pC/N). When the d₃₁′ is eliminated/reduced, the crystal is rotated around the Z-axis by an angle:

$\theta_{31} = {\arctan\left( \sqrt{\frac{- d_{31}}{d_{32}}} \right)}$ When the d₃₂′ is eliminated/reduced, the crystal is rotated around the Z-axis by an angle:

$\theta_{32} = {\arctan\left( \sqrt{\frac{- d_{32}}{d_{31}}} \right)}$

In another embodiment having this composition, the electrodes are on the (−110) faces, with a k₁₅ of about 90%, a d₁₅ of about 2000 pC/N and a d₁₆ of about 50 pC/N in which shear mode properties of yPIN-(1−y−z)PMN-zPT crystals in particular has improved AC field stability under high drive. The coercive field is about 5 kV/cm, with allowable AC field drive level about 40% of the coercive field, being on the order of about 2kV/cm.

In another embodiment having this composition, the electrodes are on the (110) faces, with a d₃₂ of about 1270 pC/N, d₃₁ of about −460 pC/N and a rotation around the Z-axis of about 31.5°. The d₃₆ is about 1540 pC/N, d₃₁′ is about 780 pC/N and d₃₂′ is about −20 pC/N.

In another embodiment, the piezoelectric single crystal previously described is doped with between about 0.2 mol % and about 8 mol % of a dopant selected from the group consisting of manganese, iron, cobalt, nickel, aluminum, gallium, copper, potassium sodium, fluorides and combinations therefore. The dopants may be provided by introducing one or more of the following compounds into the composition: MnO₂, MnCO₃, Fe₂O₃, Co₂O₃, CoCO₃, Ni₂O₃, NiCO₃, Al₂O₃, Ga₂O₃, Cu₂O, CuO, K₂CO₃, Na₂CO₃, fluoride and/or combinations thereof. Single crystals having such doped compositions also result in temperature stable piezoelectric shear properties. Preferably, the dopant is present at between about 1 mol % and about 3 mol % and in some preferred embodiments, the dopant is manganese (introduced, e.g., by MnO₂ and/or MnCO₃).

In one embodiment, x=0.29, y=0.26, z=0.29, and the crystal is doped with about 1.5 mol %, manganese. In another embodiment, the crystal has a vibration direction of [−110], a k_(is) of about 90% and a d₁₅ of about 2000 pC/N; shear mode properties of yPIN-(1−y−z)PMN-zPT crystals in particular has improved AC field stability under high drive. The coercive field is about 7 kV/cm to about 9 kV/cm for doped crystals, with internal bias field of about 1 kV/cm. The allowable AC field drive level increase to between about 60 and about 70% of the coercive field, due to the internal bias.

In one embodiment, the crystal is doped with 1.5 mol %, manganese. In another embodiment, the crystal has the electrodes on the (−110) faces, a k₁₅ of about 90%, a d₁₅ of about 2000 pC/N and a d₁₆ of about 0 pC/N; shear mode properties of yPIN-(1−y−z)PMN-zPT crystals in particular has improved AC field stability under high drive. The coercive field is about 7 kV/cm to about 9 kV/cm for doped crystals, with internal bias field of about 1 kV/cm. The allowable AC field drive level increase to between about 60 and about 70% of their respective coercive fields, due to the internal bias.

In one embodiment, a piezoelectric single crystal has a composition of the formula yPIN-(1−y−z)PMN-zPT, where 0.26≦y≦0.50, 0.20≦z≦0.31. The crystal is poled along the [111] crystallographic direction, has electrodes on the (1-10) faces and a ‘1R’ domain configuration. The crystal is rotated around the X-axis by an angle:

$\gamma = {\arctan\left( \frac{d_{16}}{d_{15}} \right)}$ The crystal exhibits a rotated transverse shear coefficient d₁₆ of zero or some other minimal value (i.e., less than about 100 pC/N).

In another embodiment having this composition, the crystal is rotated around the X-axis by about 25° and has a d₁₅ of about 3300 pC/N and a d₁₆ of about 0 pC/N.

In another embodiment, the piezoelectric single crystal previously described is doped with between about 0.2 mol % and about 8 mol % of a dopant selected from the group consisting of manganese, iron, cobalt, nickel, aluminum, gallium, copper, potassium sodium, fluorides and combinations therefore. The dopants may be provided by introducing one or more of the following compounds into the composition: MnO₂, MnCO₃, Fe₂O₃, Co₂O₃, CoCO₃, Ni₂O₃, NiCO₃, Al₂O₃, Ga₂O₃, Cu₂O, CuO, K₂CO₃, Na₂CO₃, fluoride and/or combinations thereof. Single crystals having such doped compositions also result in temperature stable piezoelectric shear properties. Preferably, the dopant is present at between about 1 mol % and about 3 mol % and in some preferred embodiments, the dopant is manganese (introduced, e.g., by MnO₂ and/or MnCO₃).

The single crystals described herein can be manufactured according to any suitable techniques for crystal growth and thereafter cut using any suitable cutting techniques to achieve the desired compositions and conformations.

FIG. 1 is a schematic phase diagram for relaxor-PT based crystals, where R, O and T represent a rhombohedral phase region, an orthorhombic/monoclinic (M_(C)) phase region and a tetragonal phase region. The monoclinic (M_(C)) phase region of exemplary embodiments is a slightly distorted orthorhombic phase; thus, the M_(C) phase region was analyzed as a pseudo-orthorhombic phase. FIG. 2 shows a schematic of various shear mode crystals, in which crystal A is [111]/(1-10); crystal B is [110]/(−110); crystal C is [110]/(001); crystal D is [001]/(110); and crystal E is [001]/(100).

According to one exemplary embodiment described herein, crystal C is provided having a new crystal cut [110]/(001), where [110] refers to the poling direction and (001) refers to the electrode orientation face, in relaxor-PT crystals, compositionally lying in the monoclinic phase. The compositions for Crystal C possess a good ‘1O’ orthorhombic single domain state after polarization along the [110] orientation. A shear piezoelectric coefficient d₂₄ observed in such cases reflects comparable shear piezoelectric coefficients to d₁₅ in the ‘1R’ domain state, being on the order of greater than about 2000 pC/N. The crystal C, [110]/(001) cut, exhibits good thermal stability over a wide temperature range of about −50° C. to about T_(OT) (orthorhombic to tetragonal phase transition temperature). In another embodiment, tetragonal and/or doped relaxor-PT single crystals exhibit improved AC and DC driving-field stability under large signal measurements.

The temperature stability of shear piezoelectric coefficients (d₂₄ vs d₁₅ in ‘1O’ domain state) is now briefly discussed. Shear piezoelectric response is in direct proportion to the transverse dielectric permittivity, spontaneous polarization and electrostrictive coefficient. Regardless of the occurrence of phase transitions, the variation of spontaneous polarization and electrostrictive coefficient are quite small when compared to the dielectric permittivity. Thus, the change in piezoelectric coefficient with temperature is mainly determined by the variation of the dielectric permittivity. A facilitated polarization rotation process corresponds to a ‘higher’ level of transverse dielectric permittivity and shear piezoelectric coefficient.

Two independent shear piezoelectric coefficients d₁₅ and d₂₄ are present for the case of [110] poled orthorhombic crystals (mm2 symmetry). As shown in FIG. 3, the polarization rotation paths of piezoelectric 15- and 24-modes are [110]_(C)→[100]_(C) and [110]_(C)→[111]_(C), respectively. FIG. 3 shows the two independent shear piezoelectric modes (15- and 24-) and related polarization rotation paths in orthorhombic crystals, where the arrow 302 represents the spontaneous polarization. The principle axes are [−110], [001] and [110] directions. The arrow 304 and the arrow 306 represent the [100] and [111] directions, respectively. The shear piezoelectric coefficient d₁₅ increases with temperature and/or composition as either approach an orthorhombic-tetragonal (O-T) phase boundary. The coefficient d₂₄ increases with temperature and/or composition as either approach an orthorhombic-rhombohedral (O-R) phase boundary. Thus, it can be found that the shear coefficient d₁₅ is not stable with respect to temperature for orthorhombic relaxor-PT based crystals, since the O-T phase boundary generally occurs above room temperature. In contrast to the O-T phase transition, a nearly ‘vertical’ O-R phase boundary exists in the phase diagram of relaxor-PT single crystal systems, as shown in FIG. 1. Utilizing this “vertical” phase boundary, orthorhombic crystal compositions can be selected near the O-R phase boundary in order to obtain high shear piezoelectric coefficients d₂₄, with temperature independent characteristic of d₂₄, since no O-R phase transition occurs in the studied temperature range for orthorhombic/monoclinic crystals.

FIG. 4 shows the temperature dependence of shear piezoelectric coefficients for orthorhombic PMN-xPT and yPIN-(1−y−z)PMN-zPT crystals with x=0.32, y=0.26 and z=0.33. As can be seen in FIG. 4, d₂₄ has a nearly temperature independent characteristic. For the orthorhombic crystals, the piezoelectric coefficient d₂₄ is approximately 2100 pC/N for both PIN-PMN-PT and PMN-PT crystals at room temperature, maintaining similar values over the temperature range from −50° C. to their respective O-T phase transition temperatures, which are approximately 80° C. for PMN-PT and 100° C. for PIN-PMN-PT. As previously noted, however, the coefficient d₁₅ of orthorhombic PIN-PMN-PT crystals increased from about 2300 pC/N to about 7000 pC/N with increasing temperature from about −50° C. to about 100° C.

Embodiments of the present invention also result in improved AC field drive stability. The polarization electric field behavior for pure [110]/(−110) yPIN-(1−y−z)PMN-zPT crystals, with y=0.26 and z=0.29, with a ‘2R’ engineered domain configuration is shown in FIG. 5(a), from which the coercive field EC is found to be on the order of about 5 kV/cm for [−110] oriented samples. The polarization loops as a function of cycling and electric field drive level are given in FIG. 5(b). The impedance characteristics for shear thickness vibration mode after cycling measurements (5000 cycles) at different field levels are shown in FIG. 5(c). For an AC drive field of 2 kV/cm at a frequency of 10 Hz, the polarization versus electric field (PE) loops after 5000 cycles showed exactly the same linear behavior as the 1st cycle, indicating the samples in the poled condition exhibited no domain reversal or fatigue. This demonstrated field stability was confirmed by the impedance-frequency characteristics of shear vibrated samples, as observed in FIG. 5(c), where no impedance changes with increasing field are observed. The PE loops become nonlinear with increasing the drive field, showing hysteretic behavior. The remnant polarization was found to increase significantly to of about 0.2 C/m² after 5000 cycles at a drive field of 3.5 kV/cm, demonstrating that samples were re-poled along the applied field direction [−110]. As a consequence, the shear vibration characteristic disappeared in the impedance frequency spectra; instead, a new lateral vibration mode observed in the lower frequency range, demonstrating that the samples were poled along [−110] direction with vibration direction along [110]/[001].

FIG. 6 shows the ferroelectric and shear electromechanical properties for 1.5 mol % manganese doped [110]/(−110) yPIN-(1−y−z)PMN-zPT crystals having the same y and z compositional ratios as discussed with respect to FIG. 5, with ‘2R’ engineered domain configuration, where the polarization electric field behavior is shown in FIG. 6(a). The polarization electric field behavior as a function of cycling and electric field drive level (as shown in FIG. 6(b)), with the corresponding impedance characteristics for shear thickness vibration mode after fatigue measurements at different levels are given in FIG. 6(c). For the doped crystals, the coercive field was found to be on the order of approximately 7 kV/cm, with an identified internal bias field at 1.2 kV/cm, as shown in FIG. 6(a). Without wishing to be bound by theory, it is believed the development of an internal bias is due to acceptor-oxygen vacancy defect dipoles in the crystals which move to the high-stressed areas of domain walls by diffusion, pin the domain walls, and stabilize the domains. The build-up of these parallel defect dipoles to the local polarization vector leads to an offset of P-E behavior or internal bias. For an AC drive field at the level of 2-5 kV/cm at 10 Hz frequency, the polarization versus electric field (PE) loops after 5000 cycles exhibited the same linear behavior as the 1st cycle, indicating the manganese doped crystals still remain in the [110] poled condition and that no domain reversal occurred. This field polarization stability can be confirmed by the impedance-frequency characteristic of the shear-vibrated samples, as observed in FIG. 6(c). Further increasing the AC drive field level to 6 kV/cm (near coercive field), the PE loops are larger, showing hysteretic behavior. As a consequence, the shear vibration characteristic disappeared with a new lateral vibration mode appear in the impedance frequency spectra. Thus, the combination of a high coercive field and internal bias in manganese doped PIN-PMN-PT crystals allowed a higher AC drive field level than pure crystals.

The ferroelectric and shear mode electromechanical properties for pure and manganese doped [110]/(−110) yPIN-(1−y−z)PMN-zPT crystals, with y=0.26 and z=0.33 and manganese about 1.5%, with ‘1O’ domain configurations are shown in FIG. 7 and FIG. 8, respectively. As discussed for FIG. 5 and FIG. 6, the stability of AC drive field for pure PIN-PMN-PT crystals with ‘1O’ engineered domain configuration was found to be about 2 kV/cm, while being on the order of about 5 kV/cm for the manganese doped crystals with the same domain configuration, attributable to the higher coercive field and internal bias field in the doped crystals.

FIG. 9(a) and FIG. 10(a) give the polarization hysteresis for, respectively, pure and manganese doped [001]/(100) yPIN-(1−y−z)PMN-zPT tetragonal crystals with ‘1T’ domain configurations, with y=0.26 and z=0.37. In the doped crystals, manganese doping was about 1.5 mol %. The polarization loops as a function of cycling and electric field levels are shown in FIGS. 9(b) & 10(b), with impedance characteristics for shear thickness vibration mode samples after fatigue cycling are shown in FIGS. 9(c) & 10(c), respectively. In contrast to the rhombohedral and/or monoclinic crystals, the tetragonal PIN-PMN-PT samples were found to possess relatively high coercive field, being on the order of 11 kV/cm, thus in favor of the large AC drive field, without any depoling and/or degradation of the shear mode properties until 4-5 kV/cm, while manganese doping further increased the drive field level to 6 kV/cm.

FIG. 11 shows the ferroelectric and shear mode electromechanical properties for the manganese doped [001]/(110) tetragonal PIN-PMN-PT crystals with a ‘1T’ domain configuration discussed with respect to FIG. 10(a)-(c). The polarization electric field behavior is given in FIG. 11(a); polarization loops as a function of cycling and electric field drive levels are shown in FIG. 11(b), while impedance characteristics for the shear thickness vibration mode after fatigue/cycling measurements at different levels are given in FIG. 11(c). The shear piezoelectric properties are comparable to [001]/(100) crystals, but with significantly higher allowable AC drive field, being on the order of 8 kV/cm.

The polarization electric field behavior for pure [111]/(1-10) yPIN-(1−y−z)PMN-zPT crystals, with y=0.26 and z=0.29, with a ‘1R’ single domain configuration is shown in FIG. 12(a), from which the coercive field E_(C) is found to be on the order of about 4.5 kV/cm for [1-10] oriented samples. The polarization loops as a function of cycling and electric field drive level are given in FIG. 12(b). The impedance characteristics for shear thickness vibration mode after cycling measurements (5000 cycles) at different field levels are shown in FIG. 12(c). For an AC drive field of 2 kV/cm at a frequency of 10 Hz, the polarization versus electric field (PE) loops after 5000 cycles showed the same linear behavior as the first cycle, indicating the samples in the poled condition exhibited no domain reversal or fatigue at 2kV/cm. This demonstrated field stability was confirmed by the impedance-frequency characteristics of shear vibrated samples, as observed in FIG. 12(c), where no impedance changes with increasing field are observed. The PE loops become nonlinear with increasing the drive field, showing hysteretic behavior. The remnant polarization was found to increase to about 0.01 C/m² after 5000 cycles at a drive field of 3 kV/cm, where the impedance was observed to decrease at resonance and antiresonance frequencies, indicating the safe AC drive field is about 2kV/cm.

FIG. 13 shows the ferroelectric and shear electromechanical properties for manganese doped [111]/(1-10) yPIN-(1−y−z)PMN-zPT crystals, with y=0.26 and z=0.29 and manganese about 1.5 mol %, with ‘1R’ engineered domain configuration, where the polarization electric field behavior is shown in FIG. 13(a). As shown, the polarization electric field behavior as a function of cycling and electric field drive level (shown in FIG. 13(b)), with the corresponding impedance characteristics for shear thickness vibration mode after fatigue measurements at different levels are given in FIG. 13(c). For the doped crystals, the coercive field was found to be on the order of 6.2 kV/cm, with an internal bias field at 1 kV/cm, as shown in FIG. 13(a). For an AC drive field at the level of 2-4 kV/cm at 10 Hz frequency, the polarization versus electric field (PE) loops after 5000 cycles exhibited the same linear behavior as the first cycle, indicating the Mn-doped crystals still remain in the [111] poled condition and no domain reversal occurred. This field polarization stability can be confirmed by the impedance-frequency characteristic of the shear-vibrated samples, as observed in FIG. 13(c). Further increasing the AC drive field level to 5 kV/cm (near coercive field), the PE loops are larger, showing hysteretic behavior. As a consequence, the antiresonance frequency of the thickness shear vibration was found to shift to lower frequency range, indicating degraded piezoelectric properties. The combination of high coercive field and internal bias in manganese modified PIN-PMN-PT crystals allowed much higher AC drive field level compared to pure crystals.

Table I summarizes the properties of various shear modes in pure and manganese modified relaxor-PT single crystals in accordance with exemplary embodiments in which ‘1R’, ‘1O’ and ‘1T’ are in single domain states while the ‘2R’ configuration is in a multi domain state. The coercive field(s) of pure PIN-PMN-PT with R and/or O phases were found to be on the order of 5 kV/cm, while coercive fields were 6-9 kV/cm for manganese modified crystals, with internal biases being on the order of 0.6-1.8 kV/cm. The piezoelectric shear coefficient, d₁₅, and electromechanical coupling factor, k₁₅, were found to be approximately 3000 pC/N and >90%, respectively for undoped crystals, with allowable AC drive fields at about 2 kV/cm. The manganese modified PIN-PMN-PT was found to possess comparable shear piezoelectric properties to the undoped counterpart, but with much higher allowable AC drive field levels, being on the order of 4-5kV/cm, due to their enhanced coercive fields and developed internal biases.

For the tetragonal crystals with ‘1T’ single domain state, the coercive fields were found to be improved, being on the order of 11 kV/cm, further increasing to 11.5 kV/cm when doped with manganese, with internal bias being 1.5 kV/cm. The allowable AC drive fields were found to increase, being in the range of 6.5-8.5 kV/cm. The piezoelectric and electromechanical coupling, however, were found to be about 1200 pC/N and 0.77, respectively, for Mn doped tetragonal PIN-PMN-PT crystals. It is interesting to note that the field stability levels (max allowable AC drive fields divided by their respective coercive fields) are on the order of approximately 40% for all the pure crystals, while the values increased to about 60-70% for the manganese modified crystals, due to the developed internal biases. Furthermore, it is observed with increasing internal bias levels, the field stability levels increase. Thus, both coercive field and internal bias can play a role in field stability levels.

TABLE I ac field Field Poling/ Engineered Ec E_(init) d_(ij) Nr stability Stability electrode domain Crystal (kV/cm) (kV/cm) ε (pC/N) k_(ij) (Hzm) (kV/cm) Ratio 110/−110 2R (d₁₅) PMNT- 2.6 / 6000 2500 0.90 500 <1 <40% Mn 111/1-10 1R (d₁₅) Pure 4.5 / 6000 3500 0.93 470 2   44% PIN PIN-Mn 6.2 1.0 8000 4100 0.94 410 4   65% 110/−110 2R (d₁₅) Pure 5.0 / 6500 2800 0.92 570 2   40% PIN PIN-Mn 7.3 1.2 4600 2200 0.91 520 5   68% 110/−110 1O (d₁₅) Pure 5.5 / 5600 3400 0.95 380 2   36% PIN PIN-Mn 9.0 0.6 5800 3500 0.95 360 5.5   61% 001/100 1T (d₁₅) Pure 11.0 / 15000 2200 0.85 850 4-5   41% PIN PIN-Mn 11.5 1.5 8000 1200 0.77 950 6.5   57% 001/110 1T (d₁₅) PIN-Mn 11.5 1.5 8000 1200 0.78 980 8.5   74%

Of particular significance is the low frequency constant (N₁₅) for crystals with ‘1O’ engineered domain configuration, being only 360-380 Hz-m, indicating the potential for low frequency transducer applications. For tetragonal single crystals, the piezoelectric and electromechanical properties were found to be lower than their counterparts, with compositions in the R and/or O phases. All the tetragonal crystals exhibit higher coercive fields, being >10 kV/cm, as a result, the AC drive field increase to 4-7 kV/cm, showing improved high field stability for high power applications.

The inventors have further determined that a zero or minimum response of the thickness shear component d₁₆ is obtained for pure and manganese doped rhombohedral PIN-PMN-PT crystals with ‘1R’ engineered domain configuration by rotating around the X-axis. FIG. 14 illustrates the rotation axis of the sample geometry of the PIN-PMN-PT relative to the spontaneous [111] polarization. FIG. 15 shows the measured d₁₅ and d₁₆ and trend curves for ‘1R’ domain configuration yPIN-(1−y−z)PMN-zPT, with y=0.26 and z=0.29, with different rotation angles around the X-axis. The rotation angle for zero d₁₆ was found to be about 25°. The general rotation angle around the X-axis to eliminate the transverse piezoelectric shear component for ‘1R’ domain configuration is given by:

$\gamma = {\arctan\left( \frac{d_{16}}{d_{15}} \right)}$ where the d₁₆ and d₁₅ are the values for a non-rotated [111]/(1-10) crystal.

FIG. 16, FIG. 17 and FIG. 18 show measured d₁₅ and d₁₆ strain field curves for [110]/(−110) PMN-xPT and pure and doped yPIN-(1−y−z)PMN-zPT, with x=0.29, y=0.26 and z=0.29 and manganese about 1.5 mol %, crystals with a ‘2R’ domain configuration. For the PMN-PT, the piezoelectric coefficients d₁₅ and d₁₆ were approximately 2300 pC/N and 25 pC/N, respectively. For the pure PIN-PMN-PT the d₁₅ and d₁₆ were approximately 2380 pC/N and 95 pC/N, while the d₁₅ and d₁₆ for the manganese doped PIN-PMN-PT were approximately 850 pC/N and 5 pC/N. It will be appreciated that the value of d₁₆ is about zero in this domain configuration and that the somewhat larger measurements obtained can be attributed to crystal misorientation.

FIG. 19 shows the rotational angle for elimination of either the d₃₁′ or d₃₂′ transverse width extensional piezoelectric coefficient for d₃₆ face shear [110]/(110) PMN-PT, PIN-PMN-PT and Mn-doped PIN-PMN-PT crystals with a ‘2R’ domain configuration having the compositions as described with respect to FIGS. 16-18.

FIG. 20 shows the measured rotated transverse width extensional piezoelectric strain field curves for d₃₆ face shear [110]/(110) PMN-xPT having a ‘2R’ domain configuration, with x=0.29. The d₃₁′ is about 780 pC/N and the d₃₂′ is about −20 pC/N.

While the foregoing specification illustrates and describes exemplary embodiments, it will be understood by those skilled in the art that various changes may be made and equivalents may be substituted for elements thereof without departing from the scope of the invention. In addition, many modifications may be made to adapt a particular situation or material to the teachings of the invention without departing from the essential scope thereof. Therefore, it is intended that the invention not be limited to the particular embodiment disclosed as the best mode contemplated for carrying out this invention, but that the invention will include all embodiments falling within the scope of the appended claims. 

The invention claimed is:
 1. A piezoelectric single crystal having a composition with the formula yPb(In_(1/2)Nb_(1/2))O₃-(1−y−z) Pb(Mg_(1/3)Nb_(2/3))O₃- zPbTiO₃ (“yPIN-(1−y−z)PMN-zPT”), where 0.26≦y≦0.50, 0.31<z≦0.36 and wherein the crystal is poled along the crystallographic [110] direction, the crystal having an orthorhombic/monoclinic phase and ‘1O’ single domain state in the range of about −50° C. to about T_(OT), where T_(OT) is the orthorhombic to tetragonal phase transition temperature.
 2. The crystal of claim 1, having macroscopic mm2 symmetry.
 3. The crystal of claim 1, wherein the crystal has electrodes on the (001) faces, a k₂₄ of about 85%, and a shear piezoelectric coefficient d₂₄ of about 2000 pC/N, the shear piezoelectric coefficient being substantially temperature stable in the range of about −50° C. to about T_(OT), where T_(OT) is the orthorhombic to tetragonal phase transition temperature.
 4. The crystal of claim 1, wherein the crystal has electrodes on the (−110) faces, a k₁₅ of about 90%, a shear piezoelectric coefficient d₁₅ of about 3000 pC/N, and has a substantially stable coercive field of about 5 kV/cm with an internal bias field of about 1 kV/cm such that the allowable AC field drive level is about 40% of the coercive field.
 5. The crystal of claim 1, wherein the crystal is doped with between 0.2 mol % to about 8 mol % of a dopant selected from the group consisting of manganese, iron, cobalt, nickel, aluminum, gallium, copper, potassium sodium, fluorides, and combinations thereof.
 6. The crystal of claim 5, wherein the crystal is doped with between about 1 mol % to about 3 mol % of the dopant.
 7. The crystal of claim 5, wherein the crystal is doped with about 1.5 mol % manganese.
 8. The crystal of claim 5, wherein the crystal has electrodes on the (001) faces, a k₂₄ of about 85%, and a shear piezoelectric coefficient d₂₄ of about 2000 pC/N, the shear piezoelectric coefficient being substantially temperature stable in the temperature range of about −50° C. to about T_(OT), where T_(OT) is the orthorhombic to tetragonal phase transition temperature.
 9. The crystal of claim 5, wherein the crystal has electrodes on the (−110) faces, a k₁₅ of about 90%, a shear piezoelectric coefficient d₁₅ of about 3000 pC/N, and has a coercive field of about 7 to about 9 kV/cm with an internal bias field of about 1 kV/cm, the allowable AC field drive level being about 60-70% of the coercive field.
 10. The crystal of claim 5, wherein the crystal has electrodes on the (−110) faces and a shear piezoelectric coefficient d₁₆ of about
 0. 11. The crystal of claim 1, wherein the crystal has electrodes on the (−110) faces and a shear piezoelectric coefficient d₁₆ of about
 0. 